WO2019211534A1 - Ods alloy powder, method for producing same by means of plasma treatment, and use thereof - Google Patents
Ods alloy powder, method for producing same by means of plasma treatment, and use thereof Download PDFInfo
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- WO2019211534A1 WO2019211534A1 PCT/FR2019/000067 FR2019000067W WO2019211534A1 WO 2019211534 A1 WO2019211534 A1 WO 2019211534A1 FR 2019000067 W FR2019000067 W FR 2019000067W WO 2019211534 A1 WO2019211534 A1 WO 2019211534A1
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- C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
- C22C32/0015—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides with only single oxides as main non-metallic constituents
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Definitions
- the present invention belongs to the field of alloys reinforced by dispersion of oxides (said alloy "ODS” according to the acronym for "Oxide Dispersion
- the invention more particularly relates to a powder of an ODS alloy, as well as its manufacturing process.
- Atomization is the most common method for making a metal powder. It consists in spraying in fine droplets a net of molten metal exposed to a jet of gas or a jet of water at high pressure in order to obtain the powder.
- the atomization is not suitable for the manufacture of an ODS alloy powder: it is often impossible to dispose of the essential raw material for atomization which is a base metal in massive form (such as example in the form of ingot) which would further contain reinforcements of oxides which are dispersed there more or less homogeneously.
- the oxide reinforcements do not melt at the same temperature as the base metal. They agglomerate then because of problems of wettability reinforcements in the molten base metal and differences in density between reinforcements and metal. In practice, the methods of foundry are therefore not used to form alloys
- the oxides are not formed (at best a part of the oxides may be in the form of amorphous oxides, ie not crystallized: a debate nevertheless exists within the scientific community to know if these non-crystallized oxides do not correspond in part to the corresponding constituent atoms which would be in solid solution in the metal matrix) and the corresponding reinforcements did not germinate within the ground powders particles.
- Only an additional consolidation step (for example by hot spinning or hot isostatic compression) increases the oxide reinforcements within the metal matrix to permanently obtain an ODS alloy. It is only after the formation of oxide particles that constitute as many reinforcements dispersed in the metal matrix that a real reinforced alloy is formed, and therefore that the name "alloy ODS" is fully justified.
- the ODS alloy powder thus obtained, in particular its composition, its size, its morphology and the distribution of oxide reinforcements within the metal matrix.
- One of the aims of the invention is therefore to avoid or mitigate one or more of the disadvantages described above, by proposing a new process for manufacturing an ODS alloy powder, more particularly having composition and / or microstructure that are optimized.
- the present invention thus relates to a process for manufacturing a powder of a reinforced alloy whose grains forming the particles of the powder comprise a metal matrix in the volume of which are dispersed crystallized oxide particles (ODS alloy), the method comprising the following successive steps:
- a metal master powder comprising a master alloy intended to form the metal matrix
- a complementary powder comprising at least one intermediate compound intended to be incorporated in the metal matrix, optionally in the form of a solid solution, atoms for forming the dispersed oxide particles;
- the combination of a mechanosynthesis grinding step and a plasma treatment step produces an ODS alloy powder comprising crystallized oxide particles as reinforcements of the metal matrix.
- thermal plasma also called "hot plasma”
- hot plasma is a very energetic plasma in which electrons and ions influence the behavior of the plasma.
- a thermal plasma is in opposition to a cold plasma which is less energetic and in which only the electrons influence the behavior of the plasma.
- the oxide particles generally melt at a temperature greater than that of the master alloy intended to form the metal matrix. They therefore tend to agglomerate because of their low wettability in the molten metal and their density different from that of the metal. Under such conditions, it is therefore impossible to obtain a reinforced alloy with oxide reinforcements dispersed in the metal matrix in a relatively homogeneous manner, in particular reinforcements of a nanometric size.
- the atoms intended to form the oxide particles are distributed in the metal matrix, possibly and most probably in the form of a solid solution, even if there is a debate on this subject within the scientific community. It is only during the subsequent consolidation stage that the oxide particles will germinate and then crystallize. However, this consolidation step as it is performed in the state of the art is not conducive to controlling the characteristics of the reinforcements obtained; in particular their size, their morphology, their degree of crystallization and / or their distribution in the metal matrix.
- the plasma torches are designed to process and obtain a powder whose particles are of micrometric size.
- a nanopowder namely a powder whose particles are of nanometric size
- the plasma torch must incorporate a quench ring.
- Plasma torch processing methods are very energetic and without additional quench ring equipment, those skilled in the art expect that a plasma torch treatment will not form a nanopowder, as well as nanoprecipitates within a particle of powder because ⁇ the precipitates would agglomerate there.
- crystallization comprising growth of oxide crystals to form the oxide particles.
- the master alloy generally crystallizes in bulk in all or part to form the metal matrix.
- the crystallized oxide reinforcements thus formed are dispersed homogeneously in the crystallized metal matrix in whole or in part.
- the manufacturing method of the invention therefore makes it possible to manufacture an ODS alloy with very good control of the size and the dispersion of the oxide precipitates reinforcing the metal matrix of the ODS alloy.
- the powder mixture is ground according to a mechanosynthesis process.
- the mixture of powders includes the parent metal powder and the complementary powder.
- the parent metal powder and the complementary powder mix intimately, so that all the atoms of the intermediate compound that are intended to form the particles dispersed oxide materials are incorporated, possibly and most probably in the form of a solid solution, into the master alloy which then forms the metal matrix.
- the particles of the mother powder have a median diameter (d 5 o) of between 1 ⁇ m and 200 ⁇ m, and even between 20 ⁇ m and 80 ⁇ m, typically between 60 ⁇ m and 65 ⁇ m.
- the median diameter (dso) of a powder is the size for which 50% of the population of particles in this powder is less than
- It can be determined by a technique such as the laser diffraction method via a particle size analyzer as described for example in the ISO 13320 standard (2009-12-01 edition).
- the metal master powder comprises the master alloy which may be selected from iron base alloy, nickel base alloy or aluminum base alloy.
- the iron base alloy may comprise by weight:
- the iron base alloy may be a steel, for example austenitic, martensitic or ferritic steel, where appropriate respecting the previous compositions by weight.
- the nickel base alloy may comprise by weight:
- 1 'Inconel® 600 comprising 14 to 17% chromium.
- titanium 0% to 5%
- tungsten 0% to 2% of molybdenum
- tantalum such as for example Inconel® 625 or 718 respectively comprising 20% to 23% % or 17% to 21% of chromium.
- the nickel base alloy can be an Inconel®.
- the powder mixture may comprise 0.1% to 2.5% by weight of the complementary powder, or even 0.1% to 0.5% by weight. .
- the aluminum base alloy may comprise, by weight, from 0% to 1% iron (or even from 0% to 0.5% iron), from 0% to 1% silicon and from 0% to 1% magnesium.
- compositions by weight are, for example, the following compositions by weight:
- the 1100 aluminum alloy comprising 0.95% iron, 0.05% magnesium, 0.2% copper and 0.1% zinc;
- aluminum alloy 6262 comprising up to 0.7% iron
- an aluminum alloy of the 1000 series such as, for example, the aluminum alloy 1050 containing less than 0.4% iron, less than 0.25% silicon and no magnesium
- an aluminum alloy of the 6000 series such as, for example, the aluminum alloy 6063 containing less than 0.35% iron, less than 0.6% silicon and less than 0.9% magnesium.
- Iron is most often an impurity and silicon improves the flowability of the alloy.
- the powder mixture may comprise 0.2% to 5% by weight of the complementary powder.
- the proportion of the precursor powder which precipitates in the form of oxide particles during step iii) of plasma treatment can be high thanks to the good yield of the manufacturing method of the invention.
- This proportion can typically be 80% (or even 90%) to 100%.
- the proportion of the atoms intended to form the dispersed oxide particles present in the metal matrix of the ODS alloy in a form other than a crystalline oxide particle is reduced or even close to 0 %.
- the proportion of complementary powder in the mixture of powders to be ground can be reduced. This promotes, during the plasma treatment state iii), the formation of oxide particles of reduced size (for example in the form of nanorenforts) and their homogeneous distribution in the metal matrix of the ODS alloy. This also decreases the cost of the manufacturing process. This proportion may thus be from 0.1% to 0.3%, or even 0.1% to 0.2% of additional powder in the mixture of powders to be ground.
- the complementary powder its particles generally have a median diameter (d 50 ) of between 1 ⁇ m and 80 ⁇ m. This median diameter can then be smaller than that of the mother powder, which favors the incorporation of the atoms intended to form the dispersed oxide particles within the master alloy of the parent metal powder.
- the intermediate compound intended to incorporate the atoms intended to form the dispersed oxide particles may be chosen from YFe 3 Y 2 O 3 , Fe 2 C 3 , Fe 2 Ti, FeCrWTi, TiH 2 , TiO 2 and Al 2 O 3. , Hf0 2 , Si0 2 , Zr0 2 , Th0 2 , MgO or mixtures thereof.
- a compound which is not an oxide is a precursor compound intended to form, after the chemical reaction, during the manufacturing process of the invention, the metal oxide corresponding which is present in the reinforced alloy at the end of this process, more particularly in the form of crystallized oxide particle.
- the atoms intended to form the dispersed oxide particles may therefore therefore comprise at least one metal atom selected from among yttrium, titanium, iron, chromium, tungsten, silicon, zirconium, thorium, magnesium, aluminum or hafnium.
- the intermediate compound is a metal oxide and therefore comprises at least one oxygen atom to enter the composition of the oxide particle.
- oxygen is provided by another intermediate compound of metal oxide type, optionally supplemented with oxygen present in the master alloy.
- the mixture of powders to be ground is subjected to step ii) of grinding according to a method of mechanosynthesis.
- This step can be carried out in a mill selected for example from a ball mill or an attritor.
- the gaseous grinding medium is generally an atmosphere of controlled composition. It can include hydrogen, argon, helium, nitrogen, air or mixtures thereof.
- the precursor powder obtained at the end of the grinding step ii) is then subjected to step iii) of thermal plasma treatment.
- the parameters of the plasma torch operated during the plasma treatment of step iii) are those conventionally used in the field of the manufacture of powders, for example in the following studies:
- the plasma torch used may be an inductively coupled radiofrequency plasma torch, a blown arc torch or a transferred arc torch.
- the radiofrequency plasma operates without an electrode.
- the energy transfer is carried out by inductive coupling: a magnetic field is applied on the plasma gas which circulates inside the induction coil in order to form the plasma.
- the power of the plasma torch can be between 10 kW and 80 kW (more particularly between 10 kW and 40 kW), or even between 20 kW and 80 kW (more particularly between 20 kW and 40 kW).
- the thermal plasma used in step iii) of the manufacturing method of the invention may be a plasma as described for example in the document "P. Fauchais,” Thermal plasmas: fundamental aspects “, Engineering techniques, booklet D2810 VI, 2005) "[reference 6].
- the thermal plasma may be at a plasma temperature of between 200 ° C. and 12000 ° C., for example between 700 ° C. and 4000 ° C. in order to melt aluminum or magnesium, or tungsten which melts at 3500 ° C. This temperature is generally sufficient to melt the species, more particularly those comprising a metal atom, which make up the precursor powder.
- the thermal plasma may be such that its electron density is between 10 14 and 10 26 3 nf nf 3 or 10 nf 18 3 and 10 26m 3 in particular for arc plasmas.
- the ionization energies can be between 0.5 eV and 50 eV.
- the plasma gas contained in the plasma torch is generally totally ionized.
- the plasma gas may be selected from argon, helium, nitrogen or mixtures thereof. It generally constitutes the central gas of the plasma torch, in which it can be introduced at a flow rate of between 10 liters / minute and 40 liters / minute.
- the pressure in the reaction chamber of the plasma torch may be low (for example less than 200 Pa) to promote the formation of the plasma by facilitating the ionization of the plasma gas.
- the pressure in the reaction chamber of the plasma torch is generally between 25 kPa and 100 kPa. The lower this pressure, the more the injection rate and therefore the flow rate of the precursor powder in the plasma torch is accelerated.
- the reaction chamber corresponds to the confinement tube.
- the precipitation reaction ie, germination and then growth
- the oxide particles is thermally activated and occurs almost instantaneously.
- the injection rate of the precursor powder in the plasma torch can nevertheless be adapted, more particularly according to the composition and / or the amount of powder to be treated.
- the precursor powder may be injected into the plasma torch at a flow rate of between 10 grams / minute and 45 grams / minute, preferably between 10 grams / minute and 30 grams / minute, more preferably between 10 grams / minute and 19 grams / minute. .
- This rate of introduction of the precursor powder can be regulated independently of the flow rate of the central gas, although it can be increased at least partially by increasing the flow rates of plasma gas and / or sheath gas.
- the injection of the precursor powder into the plasma torch can be performed by vibration, with an endless screw or a rotating disc.
- An injection in the upstream part (with reference to the flow of the plasmagenic gas) of the reaction chamber is generally coupled to a fast powder flow rate, whereas a downstream injection of the reaction chamber is coupled to a higher powder flow rate. slow, in particular to optimize the travel time of the precursor powder in the reaction chamber. Indeed, the upstream portion of the thermal plasma in the plasma torch is at a higher temperature which may not be optimal.
- a high flow rate of powder prevents the powder from dispersing by recirculation within the plasma. For example, a good compromise may be to adjust the height of the output of the injection probe described below so that it opens into the first third upstream of the reaction chamber.
- a plasma torch power of between 10 kW and 40 kW (or even between 10 kW and 30 kW) coupled with a precursor powder flow rate of between 10 g / minute and 30 g / minute (or even between 10 g / minute and 19 g / min). g / minutes) can improve:
- the proportion of oxide particles having precipitated typically, this improved proportion is such that 80% to 100% by weight of the metal atom contained in the whole of the reinforced alloy is in the form of crystallized oxide particles, preferably 90% to 100%, even more preferably 100%; and or
- the mean circularity coefficient of the particles of the reinforced alloy powder typically for 80% to 100% by weight of the crystallized oxide particles (preferably 90% to 100%, even more preferentially for 100%), this coefficient of Mean circularity improved is between 0.95 and 1, or even between 0, 98 and 1.
- the precursor powder and / or the plasmagenic gas may be introduced into the plasma torch via an injection probe.
- the precursor powder may be injected into the plasma torch simultaneously with the plasma gas, for example via the injection probe.
- the injection probe can be scanned on its outer surface by a cladding gas which can help stabilize the plasma and increase the efficiency of the manufacturing process of the invention.
- the cladding gas can be introduced into the plasma torch at a flow rate of between 10 liters / minute and 100 liters / minute.
- It may be chosen from argon, helium, nitrogen, hydrogen or their mixtures.
- the cladding gas may be a mixture of at least one main cladding gas and at least one complementary cladding gas.
- the main cladding gas (usually argon) can be introduced into the plasma torch at a high flow rate, for example a flow rate of between 40 liters / minute and 100 liters / minute.
- the complementary cladding gas has a good thermal conductivity, which improves the heat transfer between the plasma gas and the precursor powder.
- the additional cladding gas may be injected into the plasma torch at a rate lower than the rate of introduction of the main cladding gas, for example at a flow rate of between 1 liter / minute and 40 liters / minute.
- the particles of this powder generally have a size that is close to or identical to that of the precursor powder obtained at the end of the grinding step ii).
- the particles of the ODS alloy powder comprise the dispersed oxide particles and wholly or partly crystallized in the volume of the metal matrix of the ODS alloy.
- the oxide particles can be homogeneously distributed throughout the entire volume of the metal matrix, not just in a specific area. In particular, they do not localize in a privileged way to the grain boundaries of a powder particle of the ODS alloy, which would be detrimental to the mechanical properties of a material obtained from an ODS alloy powder ( cracks, weaker toughness, ).
- the isotropic microstructure of the reinforced alloy guarantees in particular homogeneous mechanical properties in all of the powder, and therefore in a material possibly manufactured with this powder, and whatever the mechanical stressing direction of this material.
- the oxide particles may comprise at least one oxide selected from Y 2 O 3, TXO 2, Al 2 O 3, Hf0 2, Si0 2, ZrO 2, TI1O2, MgO Al 2 O 3, Y 2 T1 2 O 7, Y 2 TÎ0 5 -
- the complementary powder when the complementary powder contains only a single intermediate compound, typically a metal oxide, it enters directly into the composition of the oxide particle dispersed in the ODS alloy, or even partially found in the matrix if a part of the complementary powder did not precipitate.
- the complementary powder comprises several intermediate compounds, one or more types of chemical combinations between these compounds can occur, which can lead to the formation of mixed oxides.
- the complementary powder comprises yttrium oxide Y 2 O 3 and titanium hydride TiH 2
- at least one oxide selected from Y 2 Ti 2 O 7 , Y 2 TiO 5 , YTlO 3 , YTi 2 0 6 can compose all or part of the oxide particle of the ODS alloy.
- the oxide comprises yttrium and / or titanium
- it is an oxide of pyrochlore structure such as, for example, Y 2 Ti 2 O 7 .
- the oxide particles formed in the ODS alloy may have a median diameter (dso) of between 1 nm and 500 nm. Preferably, it is between 1 nm and 200 nm, or even between 1 nm and 150 nm: it is therefore nanoparticles. Unexpectedly, such a result can be obtained by the manufacturing method of the invention without using a quench ring incorporated in the plasma torch.
- all or part of the particles of the reinforced alloy powder is spherical, or at least spheroidal.
- the mean circularity coefficient of the particles of the reinforced alloy powder (typically 80% to 100% by weight of the crystallized oxide particles, preferably 90% to 100%, even more preferably 100%) can thus be included between 0.95 and 1, or even between 0.98 and 1.
- the circularity coefficient of a particle is a shape descriptor that can be calculated from the following formula from the radius of the circle totally inscribed in the particle (Rinscr ) and the radius of the circle which totally circumscribes the particle (R C irc), these rays being represented in Figure 6 extracted from reference [7]:
- the mean circularity coefficient of a powder can be obtained from photographs of the particle followed by its automated numerical analysis. Preferably, several photographs of the same particle are taken from different angles. The circularity averaged for these different angles is then calculated. Once this operation is carried out on several grains, the average of all these grains of the circularity averaged for each grain results in the mean circularity coefficient of the powder.
- the mean circularity coefficient of a powder can be obtained automatically using an apparatus such as the "CAMSIZER Dynamic Image Analyzer” marketed by the company HORIBA Scientic.
- the reinforced alloy may further comprise, by weight, at least one of the following elements:
- the reinforced alloy powder can itself be crystallized in whole or in part (preferably completely crystallized).
- the microstructure of the particles of the reinforced alloy powder may be preferably monocrystalline (all the particles have the same crystalline structure), or also polycrystalline (the particles may have different crystalline structures).
- the high proportion of reinforced alloy powder that is crystallized can be used for its use in cold spray-type manufacturing processes (so-called "cold spray”).
- cold spray Other characteristics of microstructure and / or composition of the reinforced alloy obtained by the manufacturing method of the invention will be specified below.
- the invention also relates to a reinforced alloy powder obtained or obtainable by the manufacturing method as defined in the present description, in particular in one or more of the variants described for this process, such as for example the microstructure and or the composition of the reinforced alloy powder.
- the invention more particularly relates to a reinforced alloy powder, the grains forming the particles of the powder comprise a metal matrix in the volume of which are dispersed crystallized oxide particles.
- an ODS alloy has never been obtained directly in the form of powder, which has the particular advantage of providing good control of the precipitates, to be used in a cold forming process (for example of the "cold spray" type) and / or to obtain via an additive manufacturing process an ODS alloy (for example an ODS steel) having an improved density.
- This direct obtaining in powder form (thus in the form of a divided, powdery material), and not in the form of an already densified material, has the particular advantage of allowing direct use, possibly continuous, for example in batch mode, reinforced alloy powder according to the invention in a densification process allowing as specified below to obtain a solid material, and more particularly a part.
- the proportion by weight of the oxide particles which are crystallized is preferably such that the crystallized oxide particles comprise, by weight, 80% to 100%, (preferably 90% to 100%, even more preferably 100%) of the atom metallic content throughout the reinforced alloy.
- This metal atom corresponds to that initially present in the intermediate compound, for example yttrium, titanium, iron, chromium, tungsten, silicon, zirconium, thorium, magnesium, aluminum or hafnium .
- the metal matrix may comprise in dissolved form (typically at the atomic scale, for example in solid solution) and / or in the form of amorphous oxide particles; relative to the total weight of said metal atom contained in the whole of the reinforced alloy:
- the weight of the metal atom in the various zones of the reinforced alloy can be measured for example by X-ray microanalysis by Transmission Electron Microscopy (TEM) (for example for a control zone which is extrapolated to the whole of reinforced alloy), typically for measurement in the metal matrix.
- TEM Transmission Electron Microscopy
- the weight of the metal atom contained in the amorphous oxide particles and / or the crystallized oxide particles may also be determined by chemical analysis, or determined by considering that this weight is the complement to the weight of the metal atom which is contained in the single metal matrix (ie the sum of these two weights equals the total metal atom weight initially present in the complementary powder).
- the particles of the reinforced alloy may have an average circularity coefficient which is between 0.95 and 1.
- the metal matrix of the reinforced alloy can be crystallized.
- the oxide particles are distributed homogeneously in the volume of the metal matrix, in particular the oxide particles are not preferentially present at the grain boundaries of the powder particles of the reinforced alloy.
- the metal matrix may be composed of an iron base alloy, a nickel base alloy or an aluminum base alloy.
- the iron base alloy may comprise by weight:
- the iron base alloy may be a steel, for example austenitic, martensitic or ferritic steel, where appropriate respecting the previous compositions by weight.
- the nickel base alloy may comprise by weight:
- chromium such as for example Inconel® 600 comprising 14% to 17% chromium.
- chromium 10% to 40% chromium, 0.2% to 5% aluminum, 0.3% to 5% titanium, 0% to 5% tungsten, 0% to 2% molybdenum and 0% to 2% tantalum, such as for example Inconel® 625 or 718 containing respectively 20% to 23% or 17% to 21% of chromium.
- the nickel base alloy can be an Inconel®.
- the reinforced alloy may comprise 0.1% to 2.5% by weight of the oxide particles, or even 0.1% by weight at 0.5%.
- the aluminum base alloy may comprise, by weight, from 0% to 1% iron (or even from 0% to 0.5% iron), from 0% to
- compositions by weight are, for example, the following compositions by weight:
- the 1100 aluminum alloy comprising 0.95% iron, 0.05% magnesium, 0.2% copper and 0.1% zinc;
- aluminum alloy 6262 comprising up to 0.7% iron
- an aluminum alloy of the 1000 series such as, for example, the aluminum alloy 1050 containing less than 0.4% iron, less than 0.25% silicon and no magnesium;
- an aluminum alloy of the 6000 series such as, for example, the aluminum alloy 6063 containing less than 0.35% iron, less than 0.6% silicon and less than 0.9% magnesium.
- Iron is most often an impurity and silicon improves the flowability of the alloy.
- the reinforced alloy may comprise 0.2% to 5% by weight of the oxide particles.
- the proportion of oxide particles in the reinforced alloy is such that it may comprise 0.1% to 0.5% by weight of the oxide particles.
- the reinforced alloy may comprise from 0.1% to 2.5% by weight of an atom of the compound intermediate
- the intermediate compound (typically the metal atom) for forming the oxide particles, preferably from 0.1% to 1%, or even less than 0.1%.
- the intermediate compound is then generally located in the metal matrix. This percentage reflects the degree of precipitation of the intermediate compound (s) in the form of an oxide particle. It may in particular be measured by X microanalysis (for example transmission electron microscope EDX analysis) focused on a volume of the metal matrix not comprising oxide particles.
- the intermediate compound for forming the oxide particles may be YFe 3, Y 2 O 3 , Fe 2 O 3 , Fe 2 Ti, FeCrWTi, TiH 2 , TiO 2 , Al 2 O 3 , Hf0 2 , Si0 2 , Zr0 2 , Th0 2 , MgO or mixtures thereof.
- the oxide particles may comprise at least one oxide selected from Y 2 0 3, Ti0 2, A1 2 0 3, Hf0 2, Si0 2, Zr0 2, Th0 2, A1 2 0 3 MgO, Y 2 Ti 2 O 7 , Y 2 TiO 5 .
- the oxide particles may have a median diameter (dso) of between 1 nm and 500 nm, or even between 1 nm and 200 nm.
- the reinforced alloy may further comprise by weight at least one of the following:
- the invention also relates to the use of a reinforced alloy powder as defined above (namely, the reinforced alloy powder obtained or obtainable by the manufacturing method of the invention or the powder of reinforced alloy whose grains forming the particles of the powder comprise a metal matrix in the volume of which are dispersed crystallized oxide particles) according to one or more of the variants described in the present description, use in which the alloy powder of the invention is subjected to a densification process of the reinforced alloy powder, in order to manufacture a solid material (more particularly a part) or to a coating process in order to coat a support with the reinforced alloy powder (more particularly a thin thickness, typically between 20 pm and 50 mm).
- a reinforced alloy powder as defined above (namely, the reinforced alloy powder obtained or obtainable by the manufacturing method of the invention or the powder of reinforced alloy whose grains forming the particles of the powder comprise a metal matrix in the volume of which are dispersed crystallized oxide particles) according to one or more of the variants described in the present description, use in which the alloy powder of the invention is subjected
- the characteristics of the reinforced alloy powder according to the invention are particularly suitable for its densification in order to obtain a solid material, more particularly in the form of a part or its deposit on a support in the form of a coating (which, depending on the case, in particular for a relatively large thickness, may also be considered as a layer of a densified material).
- the densification process may be chosen from a wide range of densification processes for a powder (in particular an ODS alloy powder) which are well known to those skilled in the art, for example an additive manufacturing process or a powder injection molding method, for manufacturing the solid material, more particularly the part or the coating.
- the additive manufacturing process is chosen from a Selective Laser Melting (SLM) or Laser Powder Bed Fusion (L-PBF) method, selective beam melting Electron Beam Melting (EBM), Electron Powder Bed Fusion (E-PBF), Selective Laser Sintering (SLS), Laser Projection "Direct Metal Deposition” (DMD) or “laser cladding”) or binder projection (in English “binder jetting”).
- SLM Selective Laser Melting
- L-PBF Laser Powder Bed Fusion
- EBM Electron Beam Melting
- E-PBF Electron Powder Bed Fusion
- SLS Selective Laser Sintering
- DMD Laser Projection "Direct Metal Deposition”
- laser cladding laser cladding
- powder injection molding in English “powder injection molding” is an injection molding of parts from a mixture of metal or ceramic powder and polymeric binder, followed by debinding (removal of the binder) of the piece in a furnace under a controlled atmosphere (typically an atmosphere similar or identical to the gaseous grinding medium described above with the exception of hydrogen), then by consolidating it by sintering.
- the sintering temperature is for example between 350 ° C and 1220 ° C.
- CCM Camic Injection Molding
- MIM Metal Injection Molding
- the coating method can be selected from a coating method well known to those skilled in the art, for example a cold spraying process or a thermal spraying process.
- the principle of cold spraying consists in accelerating a gas (such as, for example, nitrogen, helium or argon), generally heated to a temperature of 100 ° C to 700 ° C, at supersonic speeds in a nozzle type "De Laval" then the powder material to be sprayed (here, the ODS reinforced alloy powder according to the invention) is introduced into the high pressure part (between 10 bar and 40 bar) of the nozzle and is projected "Unmelted" to the surface of the part to be coated at a speed of between 600 m / s and 1200 m / s. In contact with the workpiece, the particles undergo a plastic deformation and form on impact a dense and adherent coating.
- a gas such as, for example, nitrogen, helium or argon
- the advantage of this embodiment lies in the absence of melting of the particles, therefore in a very low risk of oxidation and possible integration in a hostile environment.
- the thermal spraying method may be selected from a flame thermal spraying method, an electric arc spraying method between two yarns or a blown plasma spraying method.
- a verb such as “to understand”, “to incorporate”, “to include”, “to contain” and its conjugated forms are open terms and therefore do not exclude the presence of element (s) and / or additional step (s) in addition to the element (s) and / or initial step (s) stated after these terms.
- these open terms also include a particular embodiment in which only the element (s) and / or initial stage (s), to the exclusion of all others, are targeted; in which case the open term also refers to the closed term “consisting of", “constituting", “composing of” and its conjugated forms.
- the use of the indefinite article “a” or “an” for an element or a step does not exclude, unless otherwise stated, the presence of a plurality of elements or steps.
- the terminal values are included in the ranges of parameters indicated;
- any percentage by weight of a component of the reinforced alloy, the master alloy, the powder mixture refers to the total weight of this alloy or mixture.
- the term "base alloy” is intended to denote metal used in particular in the composition of the master alloy or any other alloy, any alloy based on the metal in which the metal content is at least 50%. by weight of the metal of the alloy, particularly more than 90% or more than 95%.
- the base metal is, for example, iron, nickel or aluminum.
- the base alloy is preferably suitable for use in the nuclear field and / or under irradiation.
- variants described in the present description refers in particular to the variants which concern the chemical composition and / or the proportion of the constituents of this material and of any additional chemical species that it may possibly contain and in particular to the variants which concern the chemical composition, the structure, the geometry, the arrangement in space and / or the chemical composition of this element or of a constituent sub-element of the element.
- variants are for example those indicated in the claims.
- FIGS. 1A (general view) and 1B (view of a section) represent electron scanning microscopy (SEM) photographs of a precursor powder obtained after step ii) of grinding the manufacturing process of the invention. .
- Figures 2A (general view), 2B and 3A (view of a section) and 3B (zoomed view of a section focusing on the oxide precipitates) represent SEM images of a powder of a reinforced alloy obtained after step iii) of plasma treatment of the manufacturing method of the invention.
- FIG. 3C is a table showing atomic molar percentages obtained by energy dispersive X-ray spectrometry (EDX) for the oxide precipitates identified by the indexes. numerals 1 to 7 in Figure 3B.
- EDX energy dispersive X-ray spectrometry
- FIGS. 4A and 4B show a MET plate in a light field of a section of an ODS alloy obtained by the manufacturing method of the invention.
- Figures 5A to 5D show a series of snapshots for analyzing an oxide precipitate contained in the matrix of an ODS alloy powder obtained by the manufacturing method of the invention.
- Figure 5A obtained by MET light field is centered on the analyzed oxide precipitate.
- FIGS. 5B and 5C are TEM diffraction patterns obtained at an inclination of the sample holder at an angle of -2 ° according to X, respectively in raw form and in annotated form after analysis to identify the diffraction spots corresponding to the matrix and the oxide precipitate.
- Figure 5D is the corresponding annotated plate obtained by inclining the sample holder by an angle of -20 ° according to X.
- Figure 6 is a diagram illustrating the parameters Ri nscr and R circ needed to calculate the circularity of a grain of powder from a snapshot taken for a given angle.
- a parent metal powder composed of an iron master alloy (composition by weight: 14% Cr, 1% W, 0.3% Si, 0.3 % Mn and 0.2% Ni, 1000 ppm C, and the rest of Fe) is mixed with a complementary powder, comprising by weight relative to the total mixture of powders, 0.3% of a powder of titanium hydride (TiH 2 ) and 0.3% of an yttrium oxide powder (Y 2 O 3 ) as as intermediate compounds for forming oxide particles.
- the powder mixture is milled for 176 hours to mechanically form a precursor powder comprising a metal matrix composed of the master alloy in which the titanium, yttrium and oxygen atoms are incorporated.
- the precursor powder is then introduced into an inductively coupled radiofrequency plasma torch capable of delivering up to 80 kW of power (PL50 model marketed by Tekna).
- an inductively coupled radiofrequency plasma torch capable of delivering up to 80 kW of power (PL50 model marketed by Tekna).
- the plasma torch comprises a ceramic containment tube bathed in cooling water flowing at high speed along its outer wall.
- the cooling of the tube is essential to protect it from the large thermal flux generated by the plasma.
- the induction coil embedded in the body of the plasma torch and connected to the high frequency generator. This coil generates the alternating magnetic field that creates the plasma medium.
- a plasma gas also called central gas
- central gas is injected continuously.
- a cladding gas is vortexed along the inner wall of the containment tube through a quartz intermediate tube placed inside the containment tube.
- the precursor powder is injected directly into the center of the plasma discharge via a water-cooled injection probe positioned in the first upstream third of the reaction chamber of the plasma torch. It is then heated in flight and melted. Since induction plasmas operate without an electrode in contact with the plasma gas, a treatment without contamination can be realized.
- the precursor powder obtained above is subjected to a thermal plasma according to the operating conditions indicated in Table 1.
- the gas flow rates are as follows:
- main cladding gas (argon) 80 to 100 L / min;
- ODS powder according to the invention (more particularly crystallized oxide particles having in addition a mean circularity coefficient which is between 0.95 and 1) relative to the total weight of the treated powder mixture is indicated in the last column of Table 1. It is estimated in the first approximation by SEM analysis of the powders obtained at the end of the manufacturing process of the invention.
- Table 1 shows that the proportion of oxide that has precipitated is greater for moderate powers of plasma torch (typically between 10 kW and 40 kW, or even between 10 kW and 30 kW) and a moderate rate of injection of the powder. precursor in the plasma torch (typically ⁇ 30 g / min).
- - gas flows of 30 liters / minute of argon for the central gas, 100 liters / minute of argon for the main cladding gas and 10 liters / minute of helium for the complementary cladding gas (tests 4 and 12) ); or gas flows of 30 liters / minute of argon for the central gas, 60 liters / minute of argon for the main cladding gas and 40 liters / minute of helium for the complementary cladding gas (test 17); or gas flow rates of 30 liters / minute of argon for the central gas, 80 liters / minute of argon for the main cladding gas and 20 liters / minute of hydrogen for the complementary cladding gas (test 18).
- the comparison of the tests 4 and 12 also shows the perfect reproducibility of the manufacturing method of the invention, and therefore the control of the characteristics of the ODS alloy powder which it advantageously allows to obtain.
- an iron-base ODS alloy powder whose particles are spherical (more particularly with a mean circularity coefficient which is between 0.95 and 1) and comprise a determined proportion of nanoreenforcements (average size typically between 50 nm at 500 nm, preferably between 50 nm and 200 nm) of oxide homogeneously dispersed in the metal matrix of the ODS alloy
- the person skilled in the art can for example use the following operating conditions for the plasma torch , the priority parameters on which to act separately or in combination are the plasma torch power and the precursor powder flow rate:
- ⁇ a pressure in the reaction chamber of the plasma torch between 5 psi or 34 474 Pa and 14.5 psi (the atmospheric pressure)
- ⁇ power of the plasma torch between 20 kW and 40 kW (even between 20 kW and 30 kW),
- ⁇ a pressure in the reaction chamber of the plasma torch between 4 and 8 psi psi (between 27.6 kPa and 55.1 kPa)
- ⁇ main cladding gas flow rate between 80 L / min (or 60 L / min) and 100 L / min
- the precursor powder and the reinforced alloy powder obtained respectively at the end of the mechanosynthesis step and then the oxide precipitation step in the plasma torch according to test No. 4 are characterized by SEM (FIGS. IB, 2A, 2B, 3A and 3B), MET (FIGS. 4A and 4B) and EDX (table of FIG. 3C).
- the particles of the precursor powder are of variable shape (FIG. 1A) and have a non-crystallized chaotic microstructure containing no oxide particle having sprouted to form a reinforcement of the master alloy (FIG. 1B).
- the combination of steps ii) grinding and iii) plasma treatment according to the manufacturing process of the invention makes it possible to obtain an ODS-type reinforced alloy whose powder particles are essentially spherical and / or spheroidal (FIGS. 2D, 2B and 3A) and consist of grains composed of a crystallized metal matrix in which are incorporated by homogeneous manner of the crystallized particles of oxide appearing in the form of black dots on the gray background of varying hue constituting the metal matrix of the grains (FIGS. 2B, 3A and 3B).
- the crystallized particles of oxide are nanorenforts, their median diameter d50 being between 150 nm and 200 nm. Many precipitates smaller than 5 nm are also present.
- EDX analyzes were also performed by electron microscopy MEB and MET. They are grouped together in the table of FIG. 3C which shows that the nanorenches present in the zones 1 to 5 within the particles of the ODS alloy powder are rich in titanium, yttrium and oxygen.
- the corresponding EDX analyzes carried out in zones 6 and 7 of the metal matrix show the absence of oxygen, titanium, aluminum and yttrium in the matrix (molar% ⁇ 0.1% at margin of uncertainty close to zero when no value is indicated as for aluminum and yttrium).
- Figures 5B, 5C and 5D are obtained by TEM diffraction of the area shown in Figure 5A which is centered on an oxide precipitate of the ODS alloy of the invention. They exhibit superstructure diffraction peaks (i.e. one spot in two is brighter) which are characteristic of a pyrochlore type oxide Y 2 Ti 7 conventionally obtained in an iron-base ODS alloy.
Abstract
Description
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US17/052,076 US20210230722A1 (en) | 2018-05-03 | 2019-05-03 | Ods alloy powder, method for producing same by means of plasma treatment, and use thereof |
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KR1020207031635A KR102432787B1 (en) | 2018-05-03 | 2019-05-03 | ODS alloy powder, production method thereof by plasma treatment, and use thereof |
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KR102370831B1 (en) * | 2020-10-26 | 2022-03-07 | 한국생산기술연구원 | Nanoparticle dispersion strengthened titanium powder with improved uniformity and manufacturing method thereof |
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CN116033982A (en) * | 2022-05-30 | 2023-04-28 | 清华大学 | Alloy and preparation method thereof |
CN115449659B (en) * | 2022-08-01 | 2024-01-30 | 中南大学深圳研究院 | Oxide dispersion strengthening nickel-based superalloy, and preparation method and application thereof |
CN116477940B (en) * | 2023-03-17 | 2024-04-12 | 电子科技大学 | Yttrium titanate doped zirconia ceramic material and preparation method and application thereof |
CN116287873B (en) * | 2023-05-19 | 2023-08-04 | 北京煜鼎增材制造研究院股份有限公司 | Nickel-based superalloy for 1100 ℃ and additive manufacturing method thereof |
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Cited By (2)
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KR102370831B1 (en) * | 2020-10-26 | 2022-03-07 | 한국생산기술연구원 | Nanoparticle dispersion strengthened titanium powder with improved uniformity and manufacturing method thereof |
KR102370830B1 (en) * | 2020-10-26 | 2022-03-07 | 한국생산기술연구원 | Nanoparticle dispersion strengthened titanium powder and manufacturing method thereof |
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